Formation of contact and multiple cyclic cassiterite twins in SnO2-based ceramics co-doped with cobalt and niobium oxides

The formation of contact and cyclic cassiterite twins during crystal growth is controlled by oriented nucleation of SnO2 domains on nanosized grains of structurally related cobalt–niobium oxide phases.


Introduction
Understanding the formation of twins during crystal growth, i.e. growth twins is one of the fundamental challenges in mineralogy and materials science that remains incompletely understood (Shahani & Voorhees, 2016). The presence of growth twins influences the crystal morphology via the development of reentrant angles and, it is commonly observed that growth twins are larger than untwinned crystals due to their faster growth along the twin boundary planes (Shahani & Voorhees, 2016;Otá lora & García-Ruiz, 2014). Both effects suggest that growth twins have the potential to be exploited for the fabrication of materials with tailored properties via controlling the crystal shape and size. Therefore, it is important to understand the process of growth twinning in detail.
This work addresses the origin of contact and multiple cyclic twins of cassiterite (SnO 2 ) that form in polycrystalline SnO 2based ceramics when SnO 2 is sintered with small amounts of cobalt oxide and niobium oxide (dual-doped SnO 2 ). The typical microstructure of SnO 2 with the addition of 1 mol% of CoO and 1 mol% of Nb 2 O 5 after sintering at 1430 C for 5 h is shown in Fig. 1(a). In our previous studies, we described microstructure development and electrical properties of the ceramics (Tominc et al., 2018), and analyzed the morphology of multiple twins using electron back-scatter diffraction (EBSD) (Padró n-Navarta et al., 2020). We have shown that small addition of both aliovalent dopants in the Co:Nb ratio of up to 1:2 is necessary for efficient densification of the ceramics and growth of SnO 2 grains (Tominc et al., 2018). We also observed that dual doping results in the abundant formation of (101) twin boundaries (TBs) in cassiterite grains during SnO 2 grain growth (Tominc et al., 2018;Padró n-Navarta et al., 2020). Grains with a single (101) TB or contact twins are the most common among the twinned grains, whereas multiple cyclic twins represent only around 6% of all grains. Cyclic twins of two types were identified by EBSD, coplanar and alternating, both types occur in similar fractions and are randomly distributed in the microstructure.
Multiple twins are frequently observed in rutile (TiO 2 ) and cassiterite. The minerals are isostructural and are characterized by the 4/m 2/m 2/m point group, which has four equivalent {101} reflection planes and each can represent a twin contact. This may lead to the formation of subsequent multiple twins with a variety of morphologies (see chapter 3.3.6.9. in Hahn & Klapper, 2006). In this work, we focus on a special type of multiple twins, i.e. the cyclic twins, in which all TBs radiate from a common twin core. Both types of cyclic twins, with coplanar and alternating morphology, can be derived from a contact (101) twin as schematically shown in Figs. 1(b)-1(d). Fig. 1(b) is a (101) Cst contact twin oriented along the [010] Cst and [111] Cst zone axes common to both twin domains. In every orientation, two sets of {101} Cst reflection planes are edge-on oriented (in each twin domain), and the other {101} Cst reflection planes are oblique to the viewing direction. Cyclic twins form when twin contacts develop on subsequent edge-on oriented {101} reflection planes with all domains aligned along the same zone axis. In coplanar cyclic twins, the twin domains have the [010] Cst axis in common [ Fig. 1(c)], whereas, in alternating cyclic twins, all twin domains are oriented along their [111] Cst zone axis [Fig. 1(d)]. A more detailed description of both types of multiple cyclic twins of cassiterite that occur in the dual-doped SnO 2 is given by Padró n-Navarta et al. (2020).
Twins of different morphology and origin have been described in synthetic SnO 2 . Deformation twins on {101} planes can be introduced into SnO 2 (and also in isostructural rutile, TiO 2 ) crystals by mechanical grinding (Suzuki et al., 1991). Twinning during crystal growth was also reported; for example, contact, polysynthetic, and cyclic growth twins on {101} planes were found in nanocrystalline SnO 2 thin films produced from amorphous oxygen-deficient SnO 2 indicating  the role of nonstoichiometry in the twinning process (Zheng et al., 1996). Abundant {101} twins in epitaxial thin films of SnO 2 produced from -SnO precursor on ð " 1 1012Þ sapphire (Al 2 O 3 ) substrate formed as a result of oriented growth and recrystallization of -SnO to SnO 2 (Pan & Fu, 2001). Contact twins also formed in Cu 2 O flux-grown SnO 2 crystals with the addition of trivalent (Fe 3+ ) and pentavalent (Nb 5+ , Ta 5+ ) cations suggesting the role of these dopants in the formation of the twins (Kawamura et al., 1999). In our previous work, we analyzed (101) TBs in the dual-doped SnO 2 (Tominc et al., 2018) by aberration-corrected scanning transmission electron microscopy and confirmed that the concentration of Co and Nb along the TB planes is slightly increased but the distribution of both elements within the interface is not uniform (Tominc et al., 2018). This indicates that these twins are not chemically induced (or impurity-induced) planar defects like, for example, basal-plane inversion boundaries in Sb-doped ZnO (Rečnik et al., 2001a) or {111} twins in Be-doped MgAl 2 O 4 spinel (Drev et al., 2013). The fact that all TBs in cyclic twins radiate from a common center suggests their formation by nucleation at the beginning of crystal growth; however, the reasons for the formation of different types of cyclic twins were not revealed yet.
Twinning has been even more thoroughly investigated in isostructural rutile, TiO 2 (Rt). Here, the effect of polymorphism on the formation of twins has been identified in natural as well as in synthesized samples. Nano-scale lamellae of the high-pressure and high-temperature polymorph of TiO 2 with the -PbO 2 structure were found at {101} TBs in rutile grains in ultrahigh-pressure metamorphic rocks (Hwang et al., 2000;Meng et al., 2008) , . Penn & Banfield (1998) have shown that oriented attachment of polymorphic TiO 2 nanoparticles can result in twinning and oriented intergrowths. Another mechanism leading to rutile crystals/domains in twinned orientation is oriented (topotaxial) recrystallization and/or epitaxial growth of/on structurally related precursor minerals (Armbruster, 1981;Force et al., 1996) (Rečnik et al., 2015;Stanković et al., 2016). In principle, oriented recrystallization can result in the development of coplanar cyclic twins of rutile, which can be theoretically composed of up to six rutile domains, separated by five {101} TBs and an additional non-crystallographic contact (Hahn & Klapper, 2006;Padró n-Navarta et al., 2020). Besides coplanar cyclic twins, alternating twins with non-planar fourfold (tetragonal) c axes and composed of eight domains due to the 45 angle between the (101) and ð01 " 1 1Þ planes (Hahn & Klapper, 2006) are also found in rutile. Well known examples of these rare natural occurrences of symmetrically developed eightlings from Magnet Cove (Arkansas, USA). According to Hahn & Klapper (2006), Magnet Cove eightlings are nucleation twins, which originate from a common point (nucleus); however, the nature of the nucleus has not been described.
While the formation of certain types of twins in rutile-type minerals is well understood, the origin of cyclic twins is still puzzling the researchers. In this work, we aim to understand the formation mechanism of different types of twins that form in SnO 2 when it is doped with cobalt and niobium oxides (Tominc et al., 2018). Twins, especially the multiple cyclic twins, abundantly form only in the dual-doped SnO 2 and their morphology is typical of nucleation twinning. To confirm the origin of cyclic twins by nucleation, we first analyzed the core of a cyclic twin by scanning transmission electron microscopy (STEM). Then we studied phase relations in SnO 2 with higher additions of cobalt and niobium oxides to reveal which secondary phases that could potentially trigger the formation of cyclic twins form during the sintering. Based on the results we explain the formation mechanism of contact and cyclic twins by epitaxial recrystallization of SnO 2 on particles of two secondary phases that form during the sintering, CoNb 2 O 6 and Co 4 Nb 2 O 9 , which are both structurally related to cassiterite and describe the development of microstructures composed of normal (untwinned) grains and twins.

Synthesis of samples
For our studies of core regions of cyclic twins, we used SnO 2 doped with low amounts of cobalt oxide and niobium oxide, where the formation of large and abundantly twinned cassiterite grains is observed [see microstructure in Fig. 1(a), and also Tominc et al. (2018) and Padró n-Navarta et al. (2020)]. The samples were prepared by the standard solid-state synthesis, where SnO 2 powder (Alfa Aesar, 99.9%, nanopowder) with the addition of 1 mol% CoO (Alfa Aesar, 95%) and 1 mol% Nb 2 O 5 (Merck, 99%) was homogenized in absolute ethanol, dried and pressed into pellets. The pellets were sintered at 1430 C for 5 h in air.
For the studies of phase changes within the SnO 2 -Co 3 O 4 -Nb 2 O 5 system and to obtain a deeper insight into the role of secondary phases on the formation of twins in dual-doped cassiterite, we prepared compositions with higher additions of both oxides. Two series of samples with Co:Nb ratio for the formation of CoNb 2 O 6 and Co 4 Nb 2 O 9 phases (Co:Nb ratio 1:2 and 2:1, respectively) were prepared. In both series we added 10, 25 and 50 mol% of Co 3 O 4 (Alfa Aesar, 99.7%) and Nb 2 O 5 mixture, in the ratio for the formation of the targeted cobaltniobium oxide phase, to the SnO 2 powder. The initial compositions of all samples are given in Table 1. In preparation of these compositions, we considered only the Co:Nb ratio and disregarded the oxygen nonstoichiometry due to the addition of Co 3 O 4 instead of CoO, since Co 3+ in Co 3 O 4 is reduced to Co 2+ above 800 C (Navrotsky et al., 2010). The powder mixtures were homogenized in absolute ethanol, pressed into pellets, and fired at 700, 800, 900, 1000, 1100, 1200 and 1300 C for 16 h in air. After each firing, the samples were crushed, homogenized in absolute ethanol, dried, and repressed into pellets for firing at higher temperature.

Characterization techniques
Atomic scale analyses of the low-doped cassiterite ceramics were performed using aberration-corrected scanning transmission electron microscopy (STEM; ARM 200CF, Jeol Ltd, Tokyo, Japan) equipped with a high-angle annular dark-field detector (HAADF) for Z-contrast imaging and energydispersive X-ray spectrometer (EDXS; Jeol Centurio) with 100 mm 2 silicon drift detector for chemical analysis at the nanoscale. Samples for STEM analyses were prepared by thinning, dimpling, and Ar ion-milling to perforation (Gatan PIPS 691, California, USA).
X-ray powder diffraction (XRD) was used for the determination of the phase composition of the samples. The analyses were performed on Bruker AXS, D4 Endeavor diffractometer, within an angular range of 2Â from 10 to 70 with a step size of 0.04 and collection time of three seconds per step. The obtained data were used for the quantification of phases by Rietveld refinement using Topas Academic v.6 software package. The quantification refinement included the whole pattern profile fit in the first step followed by unit-cell parameters fit. Additionally, temperature parameters and cation positions were fitted for the involved structural models due to the certain degree of cation disorder expected in the sintered phases.
Densification of the samples was monitored by a hot-stage microscope (EM201x, Hesse instruments). The diameter of a cylindrical sample with initial dimensions of 8 mm diameter and 5 mm height was measured during heating with 5 K min À1 up to 1450 C.
EBSD analyses were performed on CamScan X500FE Crystal Probe with inclined column optimized for EBSD and field-emission electron gun allowing high-resolution spatial analyses. The EBSD patterns were recorded at 20 kV accelerating voltage and a working distance of 20 mm. The patterns were indexed automatically using the AZtechHKL software package from Oxford Instruments. See Padró n Navarta et al.   Table 1 Compositions for the analysis of phase changes in the SnO 2 -Co 3 O 4 -Nb 2 O 5 system.
(a) Compositions for the formation of the columbite-type CoNb 2 O 6 phase X (SnO 2 ) + (100-X) (1Co 3 O 4 + 3Nb 2 O 5 ); Co:Nb = 1:2; X in mol%.  finding a cyclic twin, which is oriented close to the common zone axis ([010] for coplanar and [111] for alternating twins), with a visible nucleation core and, at the same time, located in the thin part of the sample, is relatively low. An example of an alternating cyclic twin with four domains, located in a slightly thicker, but still electron-transparent part of the sample and oriented along the common [111] zone axis is shown in Fig. 2. The cyclic twin contains three TBs extending from a common center, which is positioned near the edge of the grain [ Fig. 2(a)]. Such eccentric position of the twin core is typical for cyclic twins in cassiterite ceramics as previously observed based on SEM and EBSD analyses (Tominc et al., 2018;Padró n-Navarta et al., 2020). A high-resolution HAADF-STEM image taken around the twin core region is shown in Fig. 2(b). The bright contrast stems mainly from the heavy Sn atomic columns (cation substructure) and shows that all three TBs are edge-on oriented and lie in subsequent edge-on oriented (101) planes with a 46.5 angle between two planes. At this magnification, the common origin point of all TBs of the cyclic twin is even more obvious. All three TBs are mirrorsymmetric across the twin plane. This atomic configuration of the TB corresponds to the lowest-energy pseudo-twin model of {101} twins characterized by in-plane translation of 1 2 h111i in SnO 2 (Lee et al., 1993). In addition to the three twin boundaries (crystallographic contacts), the cyclic twin contains an additional non-crystallographic contact (NCC) between the first and the last (fourth) domain, which is incomparably shorter than the twin boundaries [Figs. 2(a) and 2(b)]. This is due to the lower degree of local atomic ordering at the NCC in comparison to crystallographic contacts like twin boundaries and hence such an interface is not energetically favored. The core region contains no visible secondary crystalline phase and can be described as a nanosized amorphous pocket [ Fig. 2(b)]. EDXS spectra were recorded in bulk SnO 2 and in the core [Fig. 2(c)]. While bulk SnO 2 contains only low amounts of Co and Nb in the form of solid solubility, the amorphous core region is significantly enriched in Co and Nb. Quantification of EDXS spectra was unreliable due to the relatively large thickness at the area of interest, low count ratio, and inconvenient sample tilt relative to the detector. EDXS analysis was performed also on the TBs, where segregation of Co or Nb was not detected by EDXS, however previous analyses of this sample using quantitative HAADF-STEM indicated low and nonuniform segregation of Co and Nb to the TB planes (Tominc et al., 2018).
Excess of Co and Nb detected in the core of the cyclic twin, however, does suggest the presence of a Co-and Nb-rich precursor phase during the nucleation stage. The question is why there is no crystalline Co-Nb phase in the core. One of the possible explanations is that the cross-section did not exactly intersect the nucleus, which has been located above or below the thin section. Another possibility is that a seed particle existed before the growth of the cyclic twin when it served as a twin nucleation core, and later, in the process of SnO 2 crystal growth at higher temperatures, it reacted with SnO 2 causing the incorporation of Co and Nb in the bulk cassiterite in the form of solid solution. This process is even more likely in the samples with low doping rates, where the addition of both dopants does not exceed the solid solubility limits of Co and Nb in SnO 2 (the estimated value of total Co and Nb solid solubility in SnO 2 is around 4-6 at%) and therefore most of the Co and Nb is incorporated into SnO 2 in the $1:2 to 1:4 ratio. The total amount of Co and Nb and the Co:Nb ratio vary within these limits inside the SnO 2 grains, whereas excess cobalt oxide reacts with SnO 2 to Co 2 SnO 4 spinel grains (Tominc et al., 2018).
The fact that cyclic twins are observed only in the samples with the addition of both aliovalent oxides (cobalt and niobium oxide) is a strong indication that the nucleation of cyclic twins is related to the formation of a cobalt-niobium oxide. The formation of such a secondary phase in the form of nanosized nuclei and its transient stability is another possible scenario of twin formation, and would agree with the theory about the formation of cyclic twins by nucleation proposed by Senechal (1980). To check the hypothesis we prepared SnO 2 samples with higher additions of Co 3 O 4 and Nb 2 O 5 and investigated which phases form during the heating and how they relate to twinning in cassiterite.

Phases in SnO 2 with higher additions of Co 3 O 4 and Nb 2 O 5
According to the literature, CoNb 2 O 6 , Co 3 Nb 4 O 14, and Co 4 Nb 2 O 9 are cobalt-niobium oxides that form during the sintering of CoO-Nb 2 O 5 in air (Goldschmidt, 1960;Weitzel, 1976;Castellanos et al., 2006). CoNb 2 O 6 crystallizes in the columbite-type structure (abbreviated as Col-t 1 ), the structure of Co 3 Nb 4 O 14 is comparable to that of rutile, and the structure of Co 4 Nb 2 O 9 is comparable to that of corundum (we use abbreviation Crn-t for this phase). CoNb 2 O 6 and Co 4 Nb 2 O 9 are both interesting in connection with nucleation twinning in cassiterite. We first synthesized both phases from stoichiometric amounts of initial oxides (Co 3 O 4 and Nb 2 O 5 , taking into account the Co:Nb atomic ratio) at 1200 C (results not shown here). To follow phase changes in the SnO 2 -Co 3 O 4 -Nb 2 O 5 system with increasing temperature, we studied compositions that contained 10, 25 and 50 mol% of Co 3 O 4 and Nb 2 O 5 in the ratio for the formation of CoNb 2 O 6 and Co 4 Nb 2 O 9 (Co:Nb ratios 1:2 and 2:1, see Table 1). Here we show only the results of XRD analyses for the samples with 50 mol% of both dopant mixtures because in these samples the phase changes are best visible due to the high addition of both oxides. The XRD patterns are shown in Fig. S1. XRD patterns of the samples with 10 and 25 mol% are similar, only the amount of secondary phases is lower. The phase composition of the samples with 50 mol% addition of the dopants mixture after firing at each temperature was quantified using the Rietveld refinement procedure and the results are shown in Figs. 3(a) and 3(b).
In the sample with the addition of cobalt and niobium oxides with Co:Nb ratio 1:2 [ Fig. 3(a)], the CoNb 2 O 6 phase starts to form already below 700 C. The reaction is completed at 1000 C, when reflections from the starting oxides Co 3 O 4 and Nb 2 O 5 are not observed anymore and only reflections from rutile-type SnO 2 and CoNb 2 O 6 are present. The two phases coexist up to 1200 C. After sintering at 1300 C, the reflections from both phases almost completely disappear (a small amount of SnO 2 remains unreacted) and a new phase is formed. Reflections of this phase could not be matched with any phase in the available databases. Preliminary analyses with SEM/EDXS have shown that the phase has an approximate composition of SnCoNb 2 O 8 and according to the XRD pattern, it has a similar structure to the low-temperature form of FeNb 2 O 6 , which has the trirutile structure (Aruga et al., 1985;Beck, 2012). This suggests that the columbite-type CoNb 2 O 6 phase reacts with SnO 2 above 1200 C to form a structurally similar quaternary oxide.
In the second series of compositions, the Co 3 O 4 and Nb 2 O 5 were added to SnO 2 in the ratio for the formation of Co 4 Nb 2 O 9 phase (Co:Nb = 2:1). The results of Rietveld analysis of XRD patterns are shown in Fig. 3(b). Also here, the columbite-type CoNb 2 O 6 is the first secondary phase that forms in the system already below 700 C. The fraction of this phase increases at 800 C; however, at 900 C its amount starts to decrease and reflections of the Co 4 Nb 2 O 9 phase (Bertaut et al., 1961) appear as a result of the reaction between CoNb 2 O 6 and the remaining cobalt oxide. After sintering at 1000 C, only SnO 2 and Co 4 Nb 2 O 9 are present in the sample and their amount is stable up to 1300 C (after sintering at 1400 C, the sample with the highest addition of Co and Nb-oxide melted). SEM/EDXS analysis has shown around 3-4 at% Sn in Co 4 Nb 2 O 9 and 4-6 at% of Co and Nb in 1:2 ratio in cassiterite grains in all samples, therefore these values are the approximate (estimated) solid solubility limits.
In ceramics, grain growth is closely related to diffusion processes and accelerated shrinkage. Densification characteristics of both compositions are shown in Fig. 3(c) and indicate that both compositions start to densify above 1100 C. In SnO 2based ceramics with lower additions of both dopants, the onset of densification is shifted even to temperatures above 1300 C (Tominc et al., 2018). These temperatures are much higher than the formation of cobalt niobium oxides and indicate that SnO 2 grain growth occurs much after the formation of both secondary phases.
The sample with 50% addition of Co 3 O 4 and Nb 2 O 5 in the ratio for the formation of Co 4 Nb 2 O 9 phase after sintering at 1300 C was analyzed by EBSD, and the sample with 10% addition of both dopants in the same ratio was inspected by TEM. Fig. 4(a) is EBSD phase map of the sample showing grains of the two identified phases, SnO 2 and Co 4 Nb 2 O 9 in blue and brown, respectively. The grain misorientation analysis has confirmed the presence of (101) twin boundaries in cassiterite grains. Interestingly, cyclic twins, especially those with more than three subsequent domains are quite rare in this sample in comparison to the low-doped ceramics (Tominc et al., 2018;Padró n-Navarta et al., 2020). This suggests that the conditions for the formation of cyclic twins are more easily fulfilled in samples with lower dopant additions. EBSD data was further used for the analysis of the orientation relationship (OR) between cassiterite and Co 4 Nb 2 O 9 grains. The misorientation angle analysis of the SnO 2 -Co 4 Nb 2 O 9 contacts [ Fig. 4(a)] reveals that certain orientations between the two phases occur with the probability that is above the uniform misorientation distribution function (MDF) indicating preferential formation of correlated orientation relationship between grains of these two phases. The analysis of the misorientation data using MTEX toolbox (Hielscher & Schaeben, 2008;Mainprice et al., 2015;Krakow et al., 2017;Grimmer, 1979;Morawiec, 1997) has shown that these misorientations are crystallographic contacts that follow the OR: (101) Cst || (110) Crn-t and (010) Cst || (001) Crn-t . In Fig. 4(a), these contacts are marked by red lines. Epitaxial OR between SnO 2 and Co 4 Nb 2 O 9 was also found in TEM. Fig. 4(b) shows a contact between a larger SnO 2 grain and a smaller Co 4 Nb 2 O 9 particle. The cassiterite grain is oriented along the [111] Cst zone axis, while the Co 4 Nb 2 O 9 grain along the pseudocubic ½ " 2 221 Crn-t zone axis with (101) Cst planes parallel to the (110) Crn-t planes of Co 4 Nb 2 O 9 . This OR is equivalent to the one determined by EBSD and confirms that cassiterite grains preferentially from this type of epitaxial contact with Co 4 Nb 2 O 9 .
Our studies of phase formation during the sintering of SnO 2 with high additions of cobalt oxide and niobium oxide (much above the solid solubility limit of Co and Nb in SnO 2 ) have shown that two secondary phases form in the system; the columbite-type CoNb 2 O 6 and Co 4 Nb 2 O 9 . While CoNb 2 O 6 is   only a transient phase that reacts with SnO 2 above 1200 C, the results of EBSD and TEM analyses revealed that larger grains of the Co 4 Nb 2 O 9 phase remain stable up to 1300 C. SnO 2 grains start to coarsen above the Co 4 Nb 2 O 9 formation temperature and frequently develop epitaxial OR with the Co 4 Nb 2 O 9 grains. Although these phases were not detected in the low-doped ceramics (Tominc et al., 2018), it may be anticipated that they do form also in the low-doped samples in the regions of local chemical inhomogeneities during the heating and act as seeds for oriented growth of SnO 2 . In the following, we explain the formation of contact and cyclic twins in the dual-doped SnO 2 -based ceramics based on the structural relationship between SnO 2 , CoNb 2 O 6 , and Co 4 Nb 2 O 9 . Reasons for a fairly high fraction of untwinned grains in the low-doped ceramics are also discussed.  Fig. 5 shows crystal structures of the three phases oriented along the zone axes that are most important for understanding the formation of contact and subsequent coplanar and alternating cyclic twins in cassiterite. The relevant structural data for the three phases are given in Table 2.

Twinning in
Cassiterite is structurally related to CoNb 2 O 6 and Co 4 Nb 2 O 9 through the hexagonal close-packed (hcp) oxygen substructure. The three phases have different arrangements of the cations within the close-packed layers ]. In cassiterite [ Fig. 5(a)], the close-packed oxygen layers are severely corrugated and extend in two directions normal to each other, i.e. along the a and b axes [the (200) Cst and (020) Cst planes] (Baur, 1981). Hence, the sixfold symmetry axis along the direction of the close-packed layers is lost and a new fourfold axis that extends along the c-axis of the structure is created (West & Bruce, 1982). The loss of the sixfold axis can be observed as a deviation of the angles between the three arrays of oxygen atoms [the (002) Cst , (101) Cst, and ð " 1 101Þ Cst planes in cassiterite] within a close-packed layer from the ideal 60 [see stereogram in Fig. 5(a)]. In a close-packed layer of cassiterite, one-half of octahedral sites are occupied by Sn 4+ cations, and these form infinite chains of edge-shared octahedra along the c-axis.
In columbite-type CoNb 2 O 6 [ Fig. 5(b)] the close-packed oxygen layers lie along the a axis, i.e. along the (600) Col-t planes. CoNb 2 O 6 is structurally similar to scrutinyite (-PbO 2 ), a high-temperature polymorph of PbO 2 (Weitzel, 1976). Within a single close-packed layer, the cations form a zigzag pattern of edge-shared octahedra. Co 2+ and Nb 5+ ions (a) Phase-colored EBSD map of SnO 2 with 50% addition of Co 3 O 4 and Nb 2 O 5 in the ratio for the formation of Co 4 Nb 2 O 9 phase sintered at 1300 C. Blue lines are (101) TBs in SnO 2 grains, whereas red lines indicate epitaxial contacts between SnO 2 (blue) and Co 4 Nb 2 O 9 (brown) with (101) Cst || (110) Crn-t and (010) Cst || (001) Crn-t . The frequency of these contacts is above the uniform misorientation distribution function (MDF) as shown in the histogram below the map. (b) TEM image of the sample with the 10% addition of both oxides in the same ratio shows a SnO 2 grain in contact with Co 4 Nb 2 O 9 particle. Selected area diffraction patterns recorded from both phases disclose epitaxial OR between both phases: ½111 Cst ð101Þ Cst k ½2 " 2 21 Crn-t (110) Crn-t . This OR is identical to the epitaxial contacts determined by EBSD. occupy subsequent layers in the 1:2 ratio; two layers are occupied by Co 2+ and every third layer by Nb 5+ . This causes tripling of the unit cell along the a axis. Octahedra in the neighboring close-packed layers are corner-shared. The distortion of oxygen arrays along the close-packed layers is smaller than in cassiterite, the angle between the (021) Col-t and ð02 " 1 1Þ Col-t edge-on planes is around 59 . Co 4 Nb 2 O 9 has trigonal structure comparable to that of corundum, in which two-thirds of the available octahedral interstices are occupied within the hcp oxygen substructure. Typical of the corundum-type structure is arrangement of the cations in a honeycomb pattern within a close-packed layer (Lee & Lagerlof, 1985). In Co 4 Nb 2 O 9 , the Co 2+ and Nb 5+ occupy the octahedral interstices in 2:1 ratio on average [Fig. 5(c)]: two out of three subsequent close-packed layers have mixed composition with Co:Nb in 1:1 ratio, whereas every third layer is occupied only with Co cations, which yields overall Co:Nb ratio of 2:1. Here, oxygen atoms within the close-packed layer are symmetrically arranged and the equivalent (110) Crn-t attice planes intersect exactly at 60 .
Orientation of the SnO 2 and Co 4 Nb 2 O 9 in schemes of Figs. 5(a) and 5(c) is based on the results of EBSD and TEM analyses (Fig. 4) where it was confirmed that (101) Cst planes are parallel to (110) Crn-t planes. This OR is central to understanding the formation of cyclic twins in cassiterite. Another possible OR would be with the c axis of cassiterite parallel to the {110} Crn-t planes of the corundum-type phase: [010] Cst || [001] Crn-t and (200) Cst || (110) Crn-t ; however, no evidence for the existence of this R was found in our samples and also the high lattice mismatch between these two planes ( Table 2) is not in favor to the formation of this OR. Orientation of the columbite-type CoNb 2 O 6 phase [ Fig. 5   Both findings support our assumption that columbite-type CoNb 2 O 6 particles can act as seed grains for epitaxial growth of SnO 2 in the dual-doped ceramics. CoNb 2 O 6 is the first secondary phase that forms between cobalt and niobium oxides during the firing of doped SnO 2 -based ceramics already around 700 C [see Fig. 3(a)]. Wittkamper et al. (2017) have shown that SnO 2 grows epitaxially on columbite-type CoNb 2 O 6 already at temperatures as low as 700 C. A similar process of epitaxial nucleation of SnO 2 on CoNb 2 O 6 seed particles may occur in polycrystalline ceramics, where heterostructural nucleation of SnO 2 on CoNb 2 O 6 seed in identical or in mirror orientation may be anticipated (Fig. 6). Nucleation in identical orientation results in the formation of normal (untwinned) cassiterite grains [ Fig. 6(a) Structures of (a,d) SnO 2 , (b,e) columbite-type CoNb 2 O 6 and (c,f) Co 4 Nb 2 O 9 phase with structure coparable to that of corundum in orientations relevant for understanding the formation of (a)-(c) contact and (d)-(f) alternating cyclic twins in cassiterite by oriented growth of SnO 2 on the two structurally related phases. Typical pattern (projected unit cell) of each phase is drawn on the structural models and these patterns will be used for schematic illustration of epitaxial twinning in Figs. 6-8. A stereogram with the most relevant lattice planes involved in the twinning process is shown below each structural model. particles that are established at lower sintering temperatures represent nuclei for the development of SnO 2 contact twins during accelerated grain growth above 1300 C [see densification curve for the dual-doped ceramics in Fig. 1 (red curve) of Tominc et al. (2018)]. An additional effect that occurs in the high-temperature sintering stage is the reaction between CoNb 2 O 6 and SnO 2 . This causes dissolution of columbite seed grains into the cassiterite matrix grains and hence, the presence of secondary phase grains at the TBs or in the form of overgrown inclusions inside cassiterite grains is never observed. Our previous HR-STEM analyses of TBs and regions in the vicinity of the contacts have revealed nonuniform local enrichment with Co and Nb and also inhomogeneous distribution of both elements inside the SnO 2 matrix (Tominc et al., 2018). This supports the hypothesis about epitaxial growth of SnO 2 on preexisting nanosized CoNb 2 O 6 seeds and their later recrystallization and diffusion of Co 2+ and Nb 5+ into the cassiterite matrix.
3.3.3. Twinning in SnO 2 and its relation to the Co 4 Nb 2 O 9 . In addition to the CoNb 2 O 6 particles with the columbite-type structure, also the Co 4 Nb 2 O 6 phase grains with structure comparable to that of corundum can act as seed grains for the nucleation of cassiterite twins. The results of EBSD and TEM analyses have revealed that the following OR preferentially occurs between SnO 2 and Co 4 Nb 2 O 9 : (101)[010] Cst || (110)[001] Crn-t (Fig. 4). The small mismatch between (101) Cst and (110) Crn-t planes (Table 2) is advantageous for the development of this OR. Epitaxial growth of SnO 2 on Co 4 Nb 2 O 9 seed grains in this OR can follow 12 possible orientations as schematically shown in Fig. 7(a). Theoretically, any two SnO 2 domains that grow on a single crystal seed particle may form a (symmetric) interface. This results in 144 combinations, and the contacts can be classified into four types: (i) low-angle tilt boundaries at 7.8 and complementary angles of 172.2 (contacts 1-2 and analogous); (ii) non-crystallographic contacts at 60 and 120 (1-3, 1-5 and analogous), (iii) {101} TBs at 67.8 (contacts 1-4 and analogous) and (iv) {301} TBs at 127.8 (contacts 1-6 and analogous). Also, nucleation of cassiterite in identical orientation resulting in the formation of single-crystal cassiterite at 0 or 180 (the structure is centrosymmetric) may occur (1-1, 2-2 . . . ). The possibilities are schematically presented in Fig. 7(b); a more detailed description of this process is given in the description of rutile exsolutions from matrix ilmenite, FeTiO 3 [see Table 1 and the corresponding explanation given by Rečnik et al. (2015)].
Epitaxial growth of SnO 2 domains in various orientations on a Co 4 Nb 2 O 9 seed grain can result in the formation of different non-crystallographic and crystallographic contacts between SnO 2 domains. However, the only contact between cassiterite domains that we found in the dual-doped ceramics  Oriented growth of SnO 2 (purple) on CoNb 2 O 6 (greenish) seed can result in (a) identical orientation of SnO 2 on opposite sides of the CoNb 2 O 6 seed particle leading to the formation of untwinned cassiterite or (b) in mirror orientation for the formation of contact (101) twin.  are crystallographic (101) TBs. This implies that this interface is the most energetically stable and develops/grows further after epitaxial growth of SnO 2 domains in twin orientation on the seed particle. We even assume that neighboring domains that form at angles close to the (101) TBs (e.g. 60 ) may recrystallize to twin contacts at the beginning of grain growth. The energy of (101) and (301) twin boundaries with different local stacking was calculated for rutile, TiO 2 by Lee et al. (1993) and they found that reflection twin with 1 2 h111i in-plane translation is the lowest energy interface in rutile. Since TiO 2 and SnO 2 are isostructural, we may assume that (101) TBs are low-energy interfaces also in cassiterite. The prevalence of (101) TBs in our ceramics samples and also the abundance of (101) twins over (301) twins in natural cassiterite crystals are also in favor of this hypothesis. Epitaxial growth of cassiterite in {101} twin orientation on Co 4 Nb 2 O 9 seed can result in the formation of simple contact twins, i.e. between cassiterite domains 1-4, 2-5 or 3-6 in Fig. 7(a). Each of these simple contact twins may represent the basis for the development of a multiple cyclic twin with either coplanar or alternating configuration.
Let us now focus on the formation of coplanar multiple cyclic twins. In our samples, we observed grains with three or four domains although theoretically coplanar cyclic twins with six domains separated by five subsequent {101} TBs and an additional non-crystallographic contact to close the cyclic twin are possible (Padró n-Navarta et al., 2020). Nucleation of a cyclic twin cannot be explained by epitaxial growth of SnO 2 domains in identical OR on a Co 4 Nb 2 O 9 seed. We believe that the formation of a coplanar cyclic twin starts with the formation of a contact twin, for example between domains 1 and 4 [ Fig. 7(c)]. The formation of additional domains on a single-crystal Co 4 Nb 2 O 9 seed grain in twin orientation with the domains 1 and 4 and, at the same time, in the expected OR between SnO 2 and Co 4 Nb 2 O 9 (with {101} Cst parallel to {110} Crn-t ) is not possible. The closest possibility is epitaxial growth of SnO 2 domains on Co 4 Nb 2 O 9 at 60 angles on both sides of the starting contact twin (domain " 5 5 next to 1 and or domain 6 next to 4). These would initially form energetically demanding non-crystallographic contacts at 60 , which would then locally recrystallize to (101) twin contact (domain " 5 5 ! " 5 5 0 and 6 ! 6 0 ). Such occurrence on only one side of the 1-4 contact twin would lead to the formation of a coplanar twin with three domains, whereas the occurrence of the process on both sides of the starting 1-4 contact twin would lead to the formation of a coplanar twin with four domains separated by three TB contacts [e.g. domains " 5 5 0 -1-4-6 0 , Fig. 7(c)]. In any case, each cyclic twin is closed by the formation of a short NCC between the end domains [e.g. 5 0 and 6 0 in Fig. 7(c)].
Besides coplanar cyclic twins, a comparable fraction of alternating cyclic twins always forms in the ceramics (Padró n-Navarta et al., 2020) indicating that the probability for the formation of coplanar and alternating twins is similar. We may presume that the initial structural element, i.e. a contact {101} twin on a Co 4 Nb 2 O 9 particle can also develop into an alternating multiple cyclic twin, where all twin domains have the [111] Cst as the common zone axis. In order to understand the crystallographic relationship between SnO 2 domains and the Co 4 Nb 2 O 9 seed, it is beneficial to study the phases in rotated view (Fig. 8). Fig. 8(a) is a scheme of alternating cassiterite twin with the maximum possible number of twin domains (i.e. seven) which are separated by six twin boundary contacts. In the dual-doped ceramics, twins with three or four subsequent domains are the most common, whereas twins with five or more domains are quite rare (Padró n-Navarta et al., 2020). This suggests that conditions for the formation of a fully developed alternating twin of cassiterite in sintered ceramics are hardly ever achieved.
Cassiterite domains in Fig. 8(a) are oriented along their [111] Cst zone axes, whereas the seed is in the ½2 " 2 21 Crn-t orientation. Cassiterite domains 1 and 4 and the Co 4 Nb 2 O 9 seed represent the basic element for the development of twins with coplanar [ Fig. 7(a)] or alternating morphology. Here, the OR between cassiterite domains 1 and 4 and the seed can alternatively be written as ð101Þ½111 Cst k ð110Þ½2  1 102Þ Crn-t and ð0 " 1 1 " 1 1Þ Cst planes, another pair of planes ð " 1 120Þ Crn-t and ð0 " 1 1 " 1 1Þ Cst lies oblique to the viewing direction (marked by yellow). This pair of planes corresponds to the expected SnO 2 -Co 4 Nb 2 O 9 OR. one of the oblique (101) Cst lattice planes nearly parallel to one of the oblique (110) Crn-t planes of the Co 4 Nb 2 O 9 seed, which corresponds to the expected SnO 2 -Co 4 Nb 2 O 9 OR; an example for SnO 2 domain B and the Co 4 Nb 2 O 9 seed is shown on the stereograms in Fig. 8(b). This OR between cassiterite and corundum may lead to the stabilization of (101) TBs between cassiterite domain B and domain 1 as the low-energy interface and subsequent recrystallization to a cyclic twin with alternating morphology. It is also interesting that in this orientation, the corundum-type structure exhibits pseudo-cubic symmetry with (110) Crn-t planes (d = 0.2587 nm) nearly perpendicular to ð " 1 114Þ Crn-t planes (d = 0.2776 nm), whcih coincides with the pseudo eightfold symmetry of the alternating twin and may additionally contribute to the stabilization of cyclic twins with alternating morphology.

Microstructure development and the formation of different types of twins in SnO 2 -based ceramics co-doped with cobalt and niobium oxides
The main goal of this work was to understand the formation of contact and multiple cyclic twins of cassiterite which commonly form when in SnO 2 -based ceramics when SnO 2 is sintered with small additions of CoO and Nb 2 O 5 (1 mol% of each dopant; Co:Nb = 1:2). Exactly this composition, in terms of the total amount of the dopants and the Co:Nb ratio, yields microstructure with the highest density, composed of large SnO 2 grains with a high fraction of twins (Tominc et al., 2018). The microstructure contains about two thirds of untwinned grains and the rest are cassiterite twins, most of which are contact (101) twins, while about 6% of all grains are multiple cyclic twins with coplanar or alternating morphologies that occur in comparable fractions (Padró n-Navarta et al., 2020). The fact that abundant twinning and especially the formation of multiple cyclic twins is not observed in the samples without the addition of both dopants implies that twinning in the dualdoped cassiterite is related to a combination of specific chemical and thermodynamic conditions during the hightemperature sintering of SnO 2 in the presence of both oxides.
It has been observed in several oxides and alloys that the addition of specific dopants/ impurities triggers the formation of crystallographic contacts like twin boundaries and similar interfaces during grain/crystal growth. For example, the formation of growth twins on {111} planes is observed in silicon flakes during their growth in aluminium-silicon eutectic alloy as a result of the addition of sodium and other modifiers (Lu & Hellawell, 1987); the formation of basal-plane inversion boundaries (IBs) in ZnO is triggered by the addition of Sb 2 O 3 , SnO 2 , and other oxides (Rečnik et al., 2001a;Daneu et al., 2000;Schmid et al., 2013), abundant formation of {111} twins in MgAl 2 O 4 spinel is observed during crystal growth in the presence of BeO (Drev et al., 2013) antiphase boundaries typically form in non-stoichiometric or doped oxide perovskites (e.g. Rečnik et al., 2001b). Characteristic of these impurity-induced planar defects is enrichment of the interface with the dopant atoms and these atoms reside in specific interstitial positions within the boundary. The local atomic structure of these interfaces is well ordered and contains structural elements found in the secondary phase that forms between the main phase and the dopant, i.e. spinel phases in the case of IBs in ZnO, taaffeite modulated phase in the case of twins in BeO-doped MgAl 2 O 4 spinel and polytypic Ruddlesden-Popper phases in the case of antiphase boundaries in perovskites. The formation of impurity-induced planar defects is an energetically favorable process and can be described as continuous adsorption of impurity atoms to the growth interface which results in the progressive formation of a 2D monolayer with different chemical compositions inside the host crystal (Lu & Hellawell, 1987). The process has a profound effect on grain/crystal growth and the development of ceramic microstructures. Grains in which the impurityinduced interfaces nucleate at the beginning of crystal growth exhibit exaggerated growth, their growth is significantly faster in the direction of the defect and these grains may also develop anisotropic morphologies, at least in the initial stages of crystal growth.
If the twin boundaries in co-doped cassiterite that we studied in this work would be classic impurity-induced defects, we would expect to find Co and/or Nb ordered inside the twin contact planes. However, the results of our previous study (Tominc et al., 2018) have shown that the twin boundaries in co-doped cassiterite contain only irregular segregation of Co and Nb to the vicinity of the twin boundaries, while an ordered arrangement of the dopants within the interface was not observed. Also, these twin boundaries do not show exaggerated growth to such extent as observed in the systems with the impurity-induced defects and this suggests that these defects form via a different mechanism. An important clue for understanding the formation of twins in co-doped cassiterite ceramics is the crystallographic relationship between SnO 2 and the Co 4 Nb 2 O 9 secondary phase: (101)[010] Cst || (110)[001] Crn-t that was found in the sample with higher dopant additions (Fig. 4). In natural rutile twins, the twin boundaries sometimes contain up to few nanometres thick layers or inclusion of structurally related phases that indicate the formation of these twins is by epitaxial growth on structurally related phases or by oriented (topotaxial) recrystallization of a structurally related precursor mineral. For example, a thin epitaxial layer of ilmenite was found at (301) rutile twin contacts (Daneu et al., 2007), whereas discrete oriented corundum-inclusions were found at (101) twin boundaries (Daneu et al., 2014), both in hydrothermally formed rutile crystals. On the other hand, (101) twins of rutile found as inclusions in high P-T garnets contain a nanometrethick slab of -PbO 2 -type TiO 2 at the interface (Hwang et al., 2000;Meng et al., 2008). Structural characteristics of epitaxial secondary phases found at the twin contacts are important indicators of geochemical conditions during the rutile crystal growth/formation.
The results of our study suggest that twins in co-doped cassiterite ceramics form according to a similar mechanism that involves oriented epitaxial growth of SnO 2 domains on grains of secondary CoNb 2 O 6 and Co 4 Nb 2 O 9 phases. These particles represent heterogeneities in the system, which act as research papers seeds and lower the energy barrier for epitaxial growth of SnO 2 (Lee et al., 2016). The structural similarities between SnO 2 and both secondary phases favor the formation of heterointerfaces. The presence of seed grains is overwritten during the high-temperature sintering when solid-state diffusion processes that govern coarsening of cassiterite grains (twin growth stage) become activated. The only (indirect) evidence for the presence of seed grains that trigger the nucleation of twins in the initial stages of crystal growth is irregular segregation of Co and Nb to the twin boundaries (Tominc et al., 2018) and local enrichment of the cyclic twin cores as shown in this work [ Fig. 2(c)]. The process is presented in Fig. 9 and described in more detail in the continuation.
The starting pellet contains mostly nanosized SnO 2 powder homogenized with the addition of 1 mol% of CoO and 1 mol% of Nb 2 O 5 (Co:Nb ratio of 1:2). The distribution of both dopants in the starting pellet is not perfectly homogenous and areas with locally higher concentrations of cobalt oxide (with larger particles in the starting powder) are likely [ Fig. 9(a)]. The first reaction that occurs during the heating is the formation of the CoNb 2 O 6 phase at around 700 C. Due to the close structural relationship between CoNb 2 O 6 and SnO 2 , the SnO 2 grain in the vicinity of the CoNb 2 O 6 phase grains can locally recrystallize onto these grains in the orientation for (101) twins [ Fig. 9(b)]. The formation of Co 4 Nb 2 O 9 phase starts at around 900 C in areas locally enriched with cobalt oxide with the reaction between CoNb 2 O 6 and excess cobalt oxide. These particles represent seeds for the formation of contact and multiple cyclic twins [ Fig. 9(c)]. In the temperature range up to 1300 C, densification of the sample is very limited, the sample behaves similarly to undoped SnO 2 , where sintering in the low-temperature range (500-1000 C) is controlled by surface diffusion, and shrinking is not observed (Leite et al., 2001). The only processes observed in this temperature range are reactions between cobalt and niobium oxides to CoNb 2 O 6 and Co 4 Nb 2 O 9 secondary phases and these reactions do not have an influence on the densification. The secondary phase particles, however, represent seeds for local recrystallization of SnO 2 , which results in the formation of twin nuclei for the grwoth of different types of twins at higher sintering temperatures. The genesis of twins in the nucleation stage as a result of the presence of impurities has been suggested already by Senechal (1980). The formation of different types of twins in dual-doped SnO 2 during heating up to 1430 C; red line is the sample densification curve according to Tominc et al. (2018). (a) Inhomogeneous distribution of the dopants (CoO, red; Nb 2 O 5 , orange) among nanosized SnO 2 (gray) particles the starting compact. (b) The formation of CoNb 2 O 6 seed particles (green) and contact twins nuclei at around 700 C and (c) the formation of Co 4 Nb 2 O 9 seeds (purple) and contact and multiple cyclic twins nuclei at around 900 C. (b) and (c) represent the twin nucleation stage, which is bound to limited densification at temperatures up to $1300 C. (d) The twin growth stage coincides with accelerated densification and SnO 2 grain growth above 1300 C. During this stage, the twin nuclei develop into cassiterite twins due to the fast growth of (101) twin contacts. The seed grains recrystallize to SnO 2 , Co 2+ and Nb 5+ are incorporated into SnO 2 grains in the form of solid solution and seed grains are no longer present at the TBs and in the cyclic twin cores in the form of crystalline particles.
At temperatures above 1300 C, densification of the sample is strongly enhanced [ Fig. 9(d)]. It is related to accelerated solid-state diffusion due to the formation of point defects as a result of aliovalent doping as described by Tominc et al. (2018). During these processes, Co and Nb are incorporated into the SnO 2 matrix in the form of solid solution. The total addition of CoO and Nb 2 O 5 in the low-doped sample (1 mol% of each dopant) is around or below the solid solubility limit of the dopants in SnO 2 matrix (our estimated value of total Co and Nb solid solubility in SnO 2 is $6 at%), therefore almost all dopants are incorporated into the SnO 2 in the low-doped sample. The columbite-type CoNb 2 O 6 phase grains will in any case react with the SnO 2 to the trirutile phase above 1200 C, therefore these grains, which represent the nuclei for contact twins readily dissolve into SnO 2 . This explains the local enrichment in Co and Nb around the twin boundaries as observed in our previous work (Tominc et al., 2018). Dissolution of the Co 4 Nb 2 O 9 grains into the SnO 2 matrix phase along with the formation of secondary Co 2 SnO 4 spinel phase particles in the reaction between excess cobalt oxide and SnO 2 can also occur in the low-doped samples, where the total dopant addition does not exceed the solid solubility limit. In our previous study we found some residual niobium oxide and Co 2 SnO 4 spinel phase particles at the grain boundaries and triple points. Both can be attributed to imperfect homogenization of the starting powders and limited diffusion during solid-state sintering. The development of cyclic twins with eccentrically positioned nuclei with long TBs and a short NCC between the first and the last twin domain is a result of the fast growth of low-energy (101) TB contacts and very limited growth of the energetically unfavorable NCC.
The described sequence of chemical reactions and epitaxial growth processes not only offers a plausible explanation for the formation of contact and multiple cyclic twins by the 'epitaxially induced twinning' mechanism during the sintering of dual-doped SnO 2 -based ceramics, but also explains the presence of untwinned grains, which represent two-thirds of all grains. Untwinned grains may simply coarsen without an epitaxial contact to a secondary cobalt-niobium oxide grain, by epitaxial growth of a single SnO 2 domain on a seed, by the growth of two or more SnO 2 domains in identical or inconvenient orientation for the formation of a (101) twin contact on a seed particle. It is also important to emphasize that higher dopant additions do not enhance the formation of twins because we found many untwinned grains also in the sample with much higher addition of both dopants [see Fig. 4(a)]. Even more interesting, this sample contained fewer multiple cyclic twins in comparison to the low-doped sample, and twins with maximum four twin domains were observed. This suggests that small, nanosized nuclei are necessary for the formation of multiple cyclic twins.

Conclusions
The results of this study indicate that the formation of contact and multiple cyclic twins in SnO 2 -based ceramics co-doped with cobalt and niobium oxides is not accidental but triggered by oriented growth of SnO 2 domains in twin orientations on structurally related nanosized seed particles of secondary phases via the so-called 'epitaxially-induced twinning' mechanism.
The formation of twins is a two-stage process. The twin nuclei form in the twin nucleation stage below 1300 C, where only local recrystallization of SnO 2 on CoNb 2 O 6 and Co 4 Nb 2 O 9 seed particles occurs. These particles have crystal structures closely related to SnO 2 and enhance the formation of heteroepitaxial contacts with SnO 2 domains in different orientations. In the twin nucleation stage, some of the SnO 2 domains are in (101) twin orientation and contacts between these domains develop into (101) TBs. These TBs then grow preferentially in the twin growth stage above 1300 C, when densification and SnO 2 grain growth are strongly accelerated as a result of diffusion processes related to the incorporation of Co and Nb into the SnO 2 matrix. This stage involves recrystallization/dissolution of the seed grains into the matrix SnO 2 and obliterates the evidence about the twin nucleation stage.
One of the most important implications of this study is that the absence of a twin nucleus in a growth twin does not necessarily imply that it was not present in the twin nucleation stage. Detailed analyses of the twin contacts and twin cores, especially in the case of multiple cyclic twins provide valuable evidence about the presence of seed particles in the nucleation stage of the twin formation.